US20210381074A1 - Method for producing high manganese steel material having excellent anti-vibration characteristics and formability, and high manganese steel produced thereby - Google Patents

Method for producing high manganese steel material having excellent anti-vibration characteristics and formability, and high manganese steel produced thereby Download PDF

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US20210381074A1
US20210381074A1 US17/282,481 US201817282481A US2021381074A1 US 20210381074 A1 US20210381074 A1 US 20210381074A1 US 201817282481 A US201817282481 A US 201817282481A US 2021381074 A1 US2021381074 A1 US 2021381074A1
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steel
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Won-Tae CHO
Eung-Soo Kim
Sung-Kyu Kim
Tae-Kyo Han
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Posco Holdings Inc
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present disclosure relates to a steel material for use in automobiles or construction steel plates, and more particularly, to a high manganese steel material having excellent anti-vibration characteristics and formability that may be used in locations in which anti-vibration characteristics for noise reduction are required, and a method of manufacturing the same.
  • high manganese (Mn) vibration-proof steel is a steel grade that converts noise energy into thermal energy due to interfacial sliding of epsilon martensite in the case of external impacts, having high anti-vibration characteristics and excellent mechanical properties, and thus is suitable for use to reduce noise.
  • anti-vibration properties of high manganese anti-vibration steel are secured by manufacturing a hot rolled or cold-rolled steel plate through a process of steelmaking-continuous casting-hot rolling or by adding a cold-rolling process thereto to prepare a hot-rolled or cold-rolled steel sheet and subsequently applying a post-heat treatment to form epsilon martensite and/or form a recrystallized structure.
  • the post-heat treatment performed to secure the anti-vibration characteristics is a high-cost heat treatment to which a time exceeding 10 minutes, preferably, more than 60 minutes is applied at a temperature of usually 900° C. or higher, which has been a factor that inhibits generalization of high manganese anti-vibration steel.
  • An aspect of the present disclosure may provide a method of manufacturing a high manganese steel material having excellent anti-vibration characteristics and formability at low cost, compared to the related art, while eliminating a post-heat treatment essentially performed to improve anti-vibration characteristics, and a high manganese steel material having excellent anti-vibration characteristics manufactured thereby.
  • a method of manufacturing a high manganese steel material having excellent anti-vibration characteristics and formability includes: heating a steel slab including, in percentages by weight, 0.1% or less of carbon (C), 8 to 30% of manganese (Mn), 3.0% or less of silicon (Si), 0.1% or less of phosphorus (P), 0.02% or less of sulfur (S), 0.1% or less of nitrogen (N), 1.0% or less (excluding 0%) of titanium (Ti), 0.01% or less of boron (B), the balance iron (F) and other inevitable impurities at 1,150 to 1,350° C.; finish hot-rolling the heated steel slab to manufacture a hot-rolled steel plate; and cooling the hot-rolled steel plate to 700° C. or lower, wherein the finish hot-rolling is performed at a finishing delivery temperature (FDT) (° C.) satisfying Relational Expression 1 below:
  • each element represents content by weight
  • a steel material manufactured by the aforementioned manufacturing method having the aforementioned alloy composition, including, by area fraction, 90% or more epsilon martensite and the balance of an austenite phase as a microstructure, being a fully recrystallized structure, and having excellent, anti-vibration characteristics and formability
  • the high manganese steel material having excellent anti-vibration characteristics and formability, even if a post-heat treatment required for improving the anti-vibration characteristics of the related art high-manganese anti-vibration steel is omitted, can be provided.
  • the present disclosure may provide high manganese vibration-proof steel at a relatively low cost by omitting the post-heat treatment, and thus, a technical effect may be obtained in terms of economics and the present disclosure may be generally used in fields requiring anti-vibration characteristics.
  • FIG. 1 is a graph showing a loss rate value at a strain of 900 (m/(m ⁇ 10 ⁇ 6 )) of an Inventive Steel and a Comparative Steel over an FDT (° C.) according to an exemplary embodiment in the present disclosure.
  • FIG. 2 is a graph showing a loss rate value at a strain of 200 to 900 (m/(m ⁇ 10 ⁇ 6 )) of the Inventive Steel and the Comparative Steel in an exemplary embodiment in the present disclosure.
  • FIG. 3 shows a microstructure image of the Inventive Steel according to an exemplary embodiment in the present disclosure.
  • FIG. 4 shows XRD measurement results of the Inventive Steel and the Comparative Steel according to an exemplary embodiment in the present disclosure.
  • FIG. 5 shows a method of measuring a loss rate against a strain according to a cantilever method.
  • the inventors studied in depth a method that may achieve both anti-vibration characteristics and excellent formability even if high-cost heat treatment is omitted.
  • the inventors found that a fraction of epsilon martensite phase in the steel could be maximized by optimizing a manufacturing process along with the control of an alloy composition, and thus, a steel material having excellent anti-vibration characteristics and formability may be provided only with a series of hot rolling processes, and completed the present disclosure.
  • a steel slab having an alloy composition described below may be prepared and hot-rolled and cooled to manufacture the high manganese steel material.
  • the content of each element means the weight content (% by weight).
  • Carbon (C) is an element that stabilizes austenite in the steel and is advantageous to secure strength. However, if the carbon content exceeds 0.1%, the fraction of dissolved C is excessively increased, which impairs hot workability and significantly reduces anti-vibration characteristics.
  • Manganese (Mn) is an essential element for stably securing austenite and epsilon martensite structures.
  • Mn is an essential element for stably securing austenite and epsilon martensite structures.
  • P phosphorus
  • the content of Mn increases, internal grain boundary oxidation occurs excessively when the slab is heated, causing oxide defects on a steel surface and surface characteristics are also deteriorated during subsequent plating.
  • Mn may be included in an amount of 8 to 30%, and more advantageously, 14 to 20%.
  • Silicon (Si) is an element that is solid solution strengthened and is advantageous in improving yield strength by reducing a grain size by a solid solution effect. If the content of Si increases, a silicon compound is formed on a surface of the steel sheet during hot rolling, resulting in poor pickling and surface quality of the hot-rolled steel sheet may be deteriorated. In addition, when excessively added, weldability is significantly reduced.
  • Si may be contained in an amount of 3.0% or less, and even if it is included as 0%, there is no difficulty in securing target physical properties.
  • Phosphorus (P) and sulfur (S) are elements that are inevitably contained in steel during production thereof, and it is advantageous for these elements to be contained as low as possible. If the content of P exceeds 0.1%, segregation may occur to reduce workability of the steel, and if the content of S exceeds 0.02%, a coarse manganese sulfide (MnS) is formed to cause a defect such as flange cracks and impair formability of the steel sheet, in particular, hole expandability of the steel sheet.
  • MnS manganese sulfide
  • P may be contained in an amount of 0.1% or less
  • S may be contained in an amount of 0.02% or less.
  • N Nitrogen
  • N is an element forming a nitride. If the N content exceeds 0.1%, the fraction of dissolved N may be excessively high, inhibiting hot workability and elongation and reducing anti-vibration characteristics.
  • Titanium (Ti) is an element that combines with carbon to form a carbide, and the formed carbide suppresses grain growth, which is advantageous for refining a grain size.
  • titanium forms a compound with C and N to obtain a scavenging effect, it is advantageous in improving anti-vibration characteristics. If the content of Ti exceeds 1.0%, excess titanium segregates to the grain boundaries to cause grain boundary embrittlement or form coarse precipitated phases to inhibit the effect of inhibiting grain growth.
  • Ti may be included in an amount of 1.0% or less, and excluding 0%.
  • B Boron (B) has the effect of preventing grain boundary cracking by forming a high-temperature compound at the grain boundary upon addition with Ti. However, if the content of B exceeds 0.01%, it is not preferable because it forms a boron compound and deteriorates the surface properties.
  • B may be contained in an amount of 0.01% or less, and even if B is included as 0%, it is not difficult to secure target physical properties.
  • the steel material of the present disclosure may further include an additional element in addition to the aforementioned alloy composition to improve physical properties.
  • Nickel (Ni) is an element that effectively contributes to securing high temperature ductility. In order to obtain the aforementioned effect, Ni may be contained in an amount of 0.005% or more, and as the content increases, it is also effective in delayed fracture resistance and in preventing slab cracking. However, Ni is an expensive element and may be contained in an amount of 2.0% or less in consideration of the cost.
  • Chromium (Cr) reacts with external oxygen during hot rolling or annealing to preferentially form a Cr-based oxide film (Cr 2 O 3 ) with a thickness of 20 to 50 ⁇ m on the steel surface, thereby preventing Mn, Si, etc. contained in the steel from eluting to a surface layer. Accordingly, there is an effect of contributing to stabilization of the steel surface layer structure and improving plating surface characteristics.
  • Cr may be contained in an amount of 0.005% or more, but if the content exceeds 5.0%, a chromium carbide may be formed to rather workability and delayed fracture resistance characteristics, which, thus, is not desirable.
  • At least one of 0.005 to 0.5% of niobium (Nb), 0.005 to 0.5% of vanadium (V), and 0.005 to 1.0% of tungsten (W) may be further included.
  • Nb may be contained in an amount of 0.005 to 0.5% when added in the present disclosure.
  • V Vanadium
  • W tungsten
  • each may be contained in an amount of 0.005% or more, but in the case of V exceeding 0.5% or in the case of W exceeding 1.0%, the precipitated phase may be excessively coarsened to reduce the effect of inhibiting grain growth and cause hot brittleness.
  • V may be added in an amount of 0.005 to 0.5%
  • W may be added in an amount of 0.005 to 1.0% when added.
  • the balance of the present disclosure is Fe. Since unintended impurities from raw materials or a surrounding environment may inevitably be mixed in a typical manufacturing process, the unintended impurities cannot be excluded. Since these impurities are known to anyone of ordinary skill in the manufacturing process, all contents are not specifically mentioned in the present specification.
  • the steel slab After preparing a steel slab having an alloy composition as described above, the steel slab may be heated, and here, the steel slab may be subjected to heating in a temperature range of 1150 to 1,350° C.
  • a temperature during heating of the steel slab is too low, a rolling load may be excessively applied during subsequent hot rolling, so it may be carried out at at least 1,150° C.
  • the heated steel slab may be hot-rolled to be manufactured as a hot-rolled steel sheet.
  • finish hot rolling at a temperature (FDT (° C.)) that satisfies the following Relational Expression 1.
  • each element represents a weight content
  • the growth and recrystallization of austenite grains to a sufficient size may be induced by performing finish hot rolling at a temperature exceeding the temperature at which full recrystallization occurs, from which an epsilon martensite phase may be stably secured in a follow-up cooling and/or coiling process.
  • a total rolling reduction ratio may be 80% or more, more preferably, 90% or more. If the total rolling reduction ratio is 80% or more during the finish hot rolling, a recrystallization driving force may be sufficiently secured.
  • cooling may be performed to room temperature, and in this case, there is an effect of securing more excellent anti-vibration characteristics compared to a high manganese anti-vibration steel manufactured by the existing post-heat treatment (see Table 3 below).
  • the cooling termination temperature decreases, the amount of residual austenite decreases, so it is more advantageous in securing the epsilon martensite phase in the final microstructure.
  • cooling may be performed through normal water cooling (e.g., a cooling rate of 10° C./s or higher), and if the cooling termination temperature is room temperature to 300° C., the cooling termination temperature may be secured through rapid cooling.
  • a cooling rate during rapid cooling is not particularly limited, but may be performed at a cooling rate of 50° C./s or more, for example, or may be performed at 200° C./s or less in consideration of equipment specifications.
  • a coiling process may be further performed at the corresponding temperature, which may be selectively performed in consideration of a thickness of a steel.
  • the high manganese steel material of the present disclosure obtained by completing the aforementioned cooling process includes an epsilon martensite phase with an area fraction of 90% or more and a fully recrystallized structure, that is, does not include a non-recrystallized structure, and thus, high anti-vibration characteristics and formability may be secured.
  • the high manganese steel material of the present disclosure may be obtained by the aforementioned manufacturing process and has the aforementioned alloy composition, an alloy composition of the steel material is replaced by the previously mentioned matters.
  • the high manganese steel material of the present disclosure preferably includes epsilon martensite having an area fraction of 90% or more (including 100%) and the balance austenite phase in a microstructure.
  • the present disclosure is a fully recrystallized structure that does not contain any non-recrystallized structure, thus securing excellent anti-vibration characteristics, and more preferably, the epsilon martensite phase may be included in an amount of 95% or more.
  • the high manganese steel material of the present disclosure contains the epsilon martensite phase in a high fraction, and a residual dislocation is effectively removed by full recrystallization, whereby a rate in which the epsilon martensite phase converts impact energy into thermal energy when an external impact is applied is increased to contribute to improvement of damping performance.
  • the high manganese steel material of the present disclosure does not include any phase other than the aforementioned phase as a microstructure.
  • the high manganese steel material of the present disclosure does not include an ( ⁇ ′)-martensite phase at all.
  • the present disclosure may form the epsilon martensite phase in a sufficient fraction and obtain excellent formability even if the high-cost heat treatment performed to manufacture the related art high manganese anti-vibration steel is omitted. Therefore, the high manganese steel material of the present disclosure will have an economically advantageous technical effect as compared to the related art high manganese anti-vibration steel.
  • a tensile test piece of JIS No. 5 was manufactured, and then yield strength (YS), tensile strength (TS), and elongation (T-El and U-El) were measured.
  • the microstructure was measured using X-ray diffraction (XRD), and a fraction of each phase was derived from a peak intensity of each phase.
  • a loss rate for strain of 200 to 900 was measured in a cantilever manner.
  • ⁇ ′-M represents an alpha′-martensite
  • ⁇ represents austenite
  • ⁇ -M represents an epsilon martensite phase
  • the Inventive Steels 1 to 6 have anti-vibration characteristics and formability equivalent to or higher than those of the high manganese anti-vibration steel (see Comparative Steel 5) subjected to a post-heat treatment in the related art.
  • FIG. 1 is a graph showing a loss rate value at a strain of 900 (m/(m ⁇ 10 ⁇ 6 )) of each sample over FDT (° C.).
  • FIG. 2 is a graph showing a loss rate value at a strain of 200 to 900 (m/(m ⁇ 10 ⁇ 6 )) of some samples.
  • FIG. 3 shows an image of a microstructure of Inventive Steel 4, and it can be seen that the microstructure is mostly formed in an epsilon martensite phase.
  • FIG. 4 shows XRD measurement results of Inventive Steel 6 and Comparative Steel 6.

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US17/282,481 2018-10-18 2018-12-10 Method for producing high manganese steel material having excellent anti-vibration characteristics and formability, and high manganese steel produced thereby Pending US20210381074A1 (en)

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KR10-2018-0124444 2018-10-18
KR1020180124444A KR102098501B1 (ko) 2018-10-18 2018-10-18 방진성 및 성형성이 우수한 고망간 강재의 제조방법 및 이에 의해 제조된 고망간 강재
PCT/KR2018/015601 WO2020080602A1 (ko) 2018-10-18 2018-12-10 방진성 및 성형성이 우수한 고망간 강재의 제조방법 및 이에 의해 제조된 고망간 강재

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KR101736637B1 (ko) 2015-12-23 2017-05-17 주식회사 포스코 방진특성이 우수한 고Mn강판 및 그 제조방법
KR101736636B1 (ko) * 2015-12-23 2017-05-17 주식회사 포스코 방진특성이 우수한 고Mn강판 및 그 제조방법
KR101726130B1 (ko) * 2016-03-08 2017-04-27 주식회사 포스코 성형성이 우수한 복합조직강판 및 그 제조방법

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